CN117881539A

CN117881539A - Films comprising blends of polyurethane and copolyester elastomers useful as automotive cladding materials

Info

Publication number: CN117881539A
Application number: CN202280058492.2A
Authority: CN
Inventors: R·E·杨; S·A·巴特; G·S·霍金斯; S·E·霍赫施特勒; 金龑; T·J·佩科里尼; W·K·施赫
Original assignee: Eastman Chemical Co
Current assignee: Eastman Chemical Co
Priority date: 2021-08-27
Filing date: 2022-08-25
Publication date: 2024-04-12
Also published as: WO2023028198A1; EP4392255A1; IL310086A; KR20240056537A; US20240239945A1

Abstract

Thermoplastic films are disclosed that include a thermoplastic polymer layer comprising a thermoplastic polyurethane polymer and a copolyester polyether polymer, and a patterned adhesive layer. The thermoplastic film exhibits a final load of about 0.02 to about 0.3 lbf when tested by a 25% thermal relaxation test at a thickness of about 0.006 inches; and exhibits a 1 minute residual strain of 2% or greater when tested by the 25% elastic recovery test.

Description

Films comprising blends of polyurethane and copolyester elastomers useful as automotive cladding materials

Background

Polyvinyl chloride (PVC) and Thermoplastic Polyurethane (TPU) are two polymers commonly used in automotive protection and re-shaping films. PVC is more commonly found in automotive refinish coating materials (Automotive Restyling Wraps) (ARW) or automotive coating materials (autops), which are colored and alter the overall appearance of the vehicle. In contrast, paint protective films (Paint Protection Films) (PPF) are typically transparent and act only as protective films. TPU is more commonly used in paint protective films because certain types of TPU are well suited to provide impact resistance, abrasion resistance, and weatherability.

TPU films for PPF protect underlying paints well from chipping and their low modulus makes them stretchable with low forces, but their elastic, resilient nature may make them difficult for installers to conform to complex composite surface geometries and to enclose fully wrapped edges. PVC films are easier to apply in the challenging fields described above, but the high modulus of PVC films makes it difficult for one to stretch them. To compensate for their higher modulus, PVC ARW films are typically made thinner than TPU PPF films. Thin PVC ARW films do not protect the underlying paint as well as TPU films; when PVC ARW is hit by stone, the film tends to permanently deform compared to TPU-based films. Such reduced film durability can result in a shorter acceptable lifetime for such products.

Both types of films are generally relatively easy to remove, a desirable feature for consumers because they enjoy the benefits of the film and if they decide to remove the film at some future time to alter the build of their car again, the underlying paint may not be damaged by the product.

Most commercially available PVC-based automotive re-shape coating films are applied without the use of an aqueous-based solution or gel between the pressure sensitive adhesive layer of the film and the automobile. To prevent air entrapment and air bubbles, PVC ARWs typically achieve air evacuation through the use of interconnected microscale air channels formed in the pressure sensitive adhesive layer during film fabrication. A disadvantage of such dry mounting techniques is that the initial tackiness may prevent residual film stresses from being more widely distributed over the length of the ARW, which may result in high localized residual stresses in the film. One way to alleviate this problem is to use a chemical tackifier between the automobile and the pressure sensitive adhesive at the edge of a sheet of mounted film to improve peel adhesion strength and prevent adhesive failure in areas of high strain. This abatement technique has the serious disadvantage of leaving behind an excessive and firmly adhering adhesive residue on the automobile after removal of the film. To remove such unwanted residues, aggressive chemical or mechanical means may be required, which may be time consuming and laborious and risk damaging the underlying paint. Another way to relieve residual internal film stress in ARW is to apply heat to the film after installation to a temperature high enough to relieve internal stress, thereby preventing adhesive failure between the automobile and the pressure sensitive adhesive.

In contrast, a common method of installing PPF is to apply water or a water-based solution, which may contain soap additives, to the surface of an automobile and/or to the surface of an exposed pressure sensitive adhesive layer of a paint protective film applied to an automobile. This provides a number of advantages during installation, including, for example, venting of trapped air bubbles when the membrane is pressed into place with a squeegee. This also makes it easier to change the position of the membrane during installation. Furthermore, the addition of an aqueous solution or gel between the automotive and paint protective films allows the films to be stretched more uniformly over a given film area—by allowing the films to be stretched slightly during installation when a squeegee is applied in the transverse direction across the films, this can distribute the residual film stress of the stretched films fairly uniformly over the length of the film. This may help to prevent high strain areas that may lead to adhesion failure between the automobile surface and the pressure sensitive adhesive due to the highly elastic nature of the film such that the film no longer adheres firmly to the automobile, particularly at the edges.

One disadvantage of using water-based mounting solutions is that the mounting area may become slippery, which may cause inconvenience in the work area. Another disadvantage of using water-based mounting solutions is that in certain areas of surface geometry having high conformability requirements, having complex shapes, or at the edges of the body panels where the installer is required to fully wrap the film from the top surface of the automobile to the underside of the automobile parts, the solution may prevent sufficient initial tack to remain adhered to the automobile. Edges of automobile hoods, trunk lids, fender slots (fenders wells) and door panels are examples of such areas. To accommodate the lack of initial tackiness of the wetted adhesive layer, the installer typically dries the film prior to application to the edges of such areas or takes action to actively dry the water from the film and automobile surfaces, or uses a tacky solution that increases the tackiness of the PSA upon application. These additional steps in the installation process may result in increased time required to perform the installation, which may increase labor costs, reduce installation throughput, and even reduce the profitability of the installer.

It would be desirable to provide a film that provides improved ease of installation, durability, weatherability, and paint protection compared to PVC automotive refinish cladding materials. Such a film would be easy to install onto simple and complex automotive surface geometries and maintain adequate adhesion to the automobile without the use of tackifying chemicals.

There remains a need for a film that has improved resistance to paint chipping compared to PVC films, while being easier to stretch than PVC films; less elastic recovery than the TPU film during installation, while exhibiting satisfactory elastic recovery for a long period of time after installation so that plastic deformation from stone impact can recover over time. Furthermore, it would be desirable to provide a stretched film that minimizes residual stress so that the film has sufficiently low residual stress even when heated unevenly to provide the film with a wider range of acceptability to variations in installer procedures. In addition, PVC films contain halogen; thus, for environmental reasons, it is advantageous to have little or no halogen content while providing films with the tensile properties described above. Furthermore, there remains a need for a film with the above improvements that can be installed without the need for slip solution, so that higher strains can be achieved and installation on complex surfaces can be faster than TPU protective films. Finally, there remains a need for a film that combines all of the above improvements that can quickly, easily, reliably, and completely wrap around the edges of a vehicle body panel without the need for relief cuts (reliefs) that could expose the paint below the vehicle, which is aesthetically undesirable if the film is used as a color modifying film.

Summary of The Invention

In one aspect, the present invention relates to a thermoplastic film comprising a thermoplastic polymer layer and a patterned adhesive layer. The thermoplastic polymer layer comprises a thermoplastic polyurethane polymer comprising the reaction product of: aliphatic diisocyanate, aliphatic polyol and chain extender; and a copolyester polyether polymer comprising the reaction product of: an aliphatic diacid; aliphatic diols, aliphatic polyether polyols, and branching agents. The thermoplastic polyurethane polymer may be present in the thermoplastic polymer layer in an amount of about 65 to about 98 weight percent; and the thermoplastic film: a final load of about 0.02 to about 0.30 lbf when tested at a thickness of about 0.006 inches by a 25% thermal relaxation test; and exhibits a 1 minute residual strain of 2% or greater when tested by the 25% elastic recovery test.

The films of the present invention have improved rock resistance compared to PVC films, are as easy or easier to stretch as thinner, less protective PVC films, and exhibit desirable elastic recovery properties while retaining similar residual forces when stretched and heated above the glass transition temperature. Other aspects of the invention are as disclosed and claimed herein.

Detailed description of the preferred embodiments

In a first embodiment, the present invention relates to a thermoplastic film comprising: a thermoplastic polymer layer comprising: a thermoplastic polyurethane polymer comprising the reaction product of: aliphatic diisocyanate, aliphatic polyol and chain extender; and a copolyester polyether polymer comprising the reaction product of: an aliphatic diacid; aliphatic diols; aliphatic polyether polyols; and a branching agent, wherein the thermoplastic polyurethane polymer is present in the thermoplastic polymer layer in an amount of about 65 to about 98 weight percent. The thermoplastic film further includes a patterned adhesive layer. The thermoplastic film exhibits a final load of about 0.05 to about 0.30 lbf when tested by a 25% thermal relaxation test at a thickness of about 0.006 inches; and exhibits a 1 minute residual strain of 2% or greater when tested by the 25% elastic recovery test.

In a second embodiment according to the first embodiment, the thermoplastic film exhibits a stress at 5% strain of no greater than 700psi when tested by ASTM D-412.

In a third embodiment, according to any of the preceding embodiments, the thermoplastic film exhibits a stress at 5% strain of about 200 to about 700psi when tested by ASTM D-412.

In a fourth embodiment according to any of the preceding embodiments, the thermoplastic film exhibits a final load of about 0.10 to about 0.20 lbf when tested by a 25% thermal relaxation test at a thickness of about 0.006 inches.

In a fifth embodiment according to any of the preceding embodiments, the thermoplastic film exhibits a 1 minute residual strain of 2% to 15% when tested by the 25% elastic recovery test.

In a sixth embodiment according to any of the preceding embodiments, the thermoplastic film exhibits a damping load when tested by an impact force damping test and a tensile load per inch at 5% strain when tested by ASTM D-412, and wherein the ratio of the damping load to the tensile load per inch at 5% strain is at least 80:1.

in a seventh embodiment according to any of the preceding embodiments, the thermoplastic film exhibits a damping load when tested by an impact force damping test and a tensile load per inch at 5% strain when tested by ASTM D-412, and wherein the ratio of the damping load to the tensile load per inch at 5% strain is about 80:1 to about 300:1.

In an eighth embodiment according to any of the preceding embodiments, the polymer blend exhibits a permanent set of about 25% to about 50% when tested according to the 50% relaxation test.

In a ninth embodiment according to any one of the preceding embodiments, the thermoplastic polyurethane polymer comprises soft segments and hard segments, and wherein the soft segments comprise from about 40 to about 50 weight percent of the thermoplastic polyurethane polymer.

In a tenth embodiment according to any of the preceding embodiments, the copolyester polyether polymer comprises poly (cyclohexylenedimethylene cyclohexanedicarboxylate), a glycol, and an acid comonomer (PCCE).

In an eleventh embodiment according to any of the preceding embodiments, the thermoplastic polyurethane polymer is present in the thermoplastic polymer layer in an amount of from about 70 to about 97 weight percent.

In a twelfth embodiment according to any of the preceding embodiments, the thermoplastic polyurethane layer further comprises one or more of the following: aliphatic polyether thermoplastic polyurethanes; ethylene Vinyl Acetate (EVA); polyvinyl chloride; thermoplastic polyamides, thermoplastic polyolefin elastomers, thermoplastic styrene block copolymers; aromatic thermoplastic copolyester ether elastomers; or polyvinyl acetals.

In a thirteenth embodiment, according to any of the preceding embodiments, the thermoplastic film is visually clear.

In a fourteenth embodiment according to any one of the preceding embodiments, the thermoplastic polyurethane is present in the thermoplastic polymer layer in an amount of from about 75 to about 95 weight percent.

In a fifteenth embodiment according to any of the preceding embodiments, the aliphatic diisocyanate comprises at least 80 mole% of one or more of 4,4' -dicyclohexylmethane diisocyanate, hexamethylene diisocyanate, or isophorone diisocyanate.

In a sixteenth embodiment according to any of the preceding embodiments, the aliphatic polyol of the thermoplastic polyurethane polymer has a Mw of about 750 to about 2,000.

In a seventeenth embodiment according to any of the preceding embodiments, the aliphatic polyol of the thermoplastic polyurethane polymer comprises an aliphatic polycaprolactone polyol.

In an eighteenth embodiment according to any of the preceding embodiments, the aliphatic polyol comprises an aliphatic polyether polyol.

In a nineteenth embodiment according to any of the preceding embodiments, the chain extender comprises a glycol having from 2 to 10 carbon atoms.

In a twentieth embodiment in accordance with any one of the preceding embodiments, the thermoplastic polyurethane polymer or thermoplastic polyurethane polymer blend has a Tg of about-30 ℃ to about 60 ℃.

In a twenty-first embodiment according to any one of the preceding embodiments, the thermoplastic polyurethane has a weight average molecular weight of 50,000 daltons to 400,000 daltons.

In a twenty-second embodiment according to any of the preceding embodiments, the thermoplastic polyurethane polymer comprises residues of hexamethylene diisocyanate, 1, 4-butanediol, and caprolactone.

In a twenty-third embodiment according to any of the preceding embodiments, the chain extender comprises 1, 4-butanediol.

In a twenty-fourth embodiment according to any of the preceding embodiments, the thermoplastic film further comprises a protective topcoat on the side of the film opposite the patterned adhesive layer.

In a twenty-fifth embodiment according to any of the preceding embodiments, the thermoplastic film has a thickness of about 50 to about 300 micrometers.

In a twenty-sixth embodiment according to any of the preceding embodiments, the copolyester polyether polymer has a Tg of about-70 ℃ to about 50 ℃.

In a twenty-seventh embodiment of any of the preceding embodiments, the copolyester polyether polymer has an inherent viscosity (IhV) of about 0.85 to about 1.40.

In a twenty-eighth embodiment of any of the preceding embodiments, the aliphatic diacid of the copolyester polyether polymer comprises cyclohexanedicarboxylic acid.

In a twenty-ninth embodiment according to any of the preceding embodiments, the aliphatic diol in the copolyester polyether polymer comprises cyclohexanedimethanol.

In a thirty-first embodiment, the branching agent in the copolyester polyether polymer comprises trimellitic anhydride.

In a thirty-first embodiment, the present invention is directed to an article coated with the thermoplastic film of any of the preceding embodiments.

In a thirty-second embodiment, the article comprises one or more of an automobile, truck, or train.

In a thirty-third embodiment, the present invention is directed to a method of applying the thermoplastic film of any of the preceding embodiments to a substrate, the method comprising:

a. exposing the patterned adhesive layer;

b. adhering the patterned adhesive layer of the thermoplastic film to at least one location on a substrate;

c. Stretching the thermoplastic film and adhering the patterned adhesive layer to another location on the substrate;

d. leveling the thermoplastic film using one or more of a hand, gloved hand, or squeegee to conform the thermoplastic film to a substrate; and

e. the thermoplastic film is wrapped around at least one edge of the substrate to conceal the underlying color of the substrate.

In a thirty-fourth embodiment, the thermoplastic film is heated during the process.

In a thirty-fifth embodiment according to any preceding method, the thermoplastic film is heated after being applied to the substrate to achieve one or more of the following: securing the membrane in place, reducing tension, or preventing separation after application.

In a thirty-sixth embodiment, the method according to any one of the preceding embodiments, wherein the at least one location on the substrate is near the middle of the substrate.

The present invention is thus directed to films, polymers and blends useful as automotive sheathing materials having improved properties compared to conventional polyvinyl chloride (PVC) automotive sheathing materials and Thermoplastic Polyurethane (TPU) PPF films.

In one aspect, the films of the present invention may be colored. The color may be provided, for example, as a pigment in the thermoplastic substrate itself, or may be provided, for example, in a patterned adhesive layer. Alternatively, the film of the present invention may include one or more coloring layers to color the surface to which the film is applied. Similarly, the films of the present invention may comprise a colored layer, a colorant or pigment in the substrate and/or the patterned adhesive layer.

PVC films containing various modifiers such as pigments, flakes and other particles are commonly used as automotive refinish films. To apply the film, the PSA is exposed by removing the silicone coated release liner and "fixing" some location of the PVC film to the vehicle, and the installer uses their hand, squeegee or other tool to planarize the film to conform it to the vehicle body. Typically, an installer adheres one area of the film to the automobile surface, grasps another portion of the film with his hand, and then presses (scrapes) the film onto the remaining automobile surface, stretching the film as it passes over the contours in the surface. The PVC film may be further stretched during application of the film to minimize or eliminate bunching and wrinkling, or to provide the film with a surface area greater than it would be in an unstretched state. Considering that these films are manually stretched, there is an upper limit to the force that an installer can withstand in order to stretch the film. The force required to stretch the film can be readily measured using standard tensile tests. In such experiments, the film was stretched at a constant deformation rate and the load was recorded with deformation. Such deformation can be easily converted into a strain value. The higher the load (normalized to the load per inch width) at a given strain value, the more difficult the stretching. Stretchability depends on the composition and thickness of the film.

It is also important for the film to not rebound quickly and recover its original length too quickly after stretching. This makes it easier for an installer to manipulate (position) the film around complex corners and shapes before pressing the film to adhere it to a surface. The property that controls the workability of the film is its elastic recovery, which can be measured as residual strain. Elastic recovery is defined as the residual strain on the film some time after load release. Preferably, the film has at least some residual strain, which may be referred to as initial strain, up to one minute after load release. In this regard, highly elastic materials with low residual strain levels (i.e., fast "rebound" rates) at 1 minute, such as TPU commonly used in PPF films, are undesirable, although they are superior to PVC films in terms of stretchability and rock resistance. In any event, it is desirable that any strain on the film eventually returns to zero, for example 24 hours after stretching.

The thickness of the film also plays a role in the primary function of the film to protect the paint from rock impact; the thicker the film, the better it protects the underlying paint from chips and other types of mechanical damage. Because the thickness of the film is related to the amount of paint chip protection (chip protection) that it can provide, thicker films are required in some cases. Paint chipping (paint chipping) caused by flying stones is related to the amount of impact force applied by the stone. This is a direct function of the mass of the block times the velocity (impact energy). Reducing (i.e., attenuating) this force will prevent chipping. Thus, the function of conventional PPF laminates is to attenuate (absorb) as much of the flyrock impact force as possible. While forces can be attenuated by both plastic and elastic deformation, PPF applications desire to maintain the appearance of the vehicle for as long as possible. Thus, elastic materials are preferred as substrates over plastic materials because they do not leave impact deformations.

Impact force can be easily measured using a piezoelectric dynamic force sensor. These sensors contain piezoelectric crystals that convert the deformation into an electrical signal proportional to the deformation. When a force is applied to this sensor, the quartz crystal generates an electrostatic charge that is proportional to the input force. The output is collected on electrodes sandwiched between crystals and then sent directly to an external charge amplifier or converted to a low impedance voltage signal in a sensor. The force measured when the rock hits the sensor can be measured with and without the PPF film applied and the amount of damping load can be easily determined by comparing these two values.

Since high fracture resistance at good stretchability is desirable, this combined property can be measured by comparing the ratio of load decay (high is good) to tensile stress per inch (low is good). The higher the ratio, the better. A composition that provides both high load attenuation and low load per inch at a given thickness is highly desirable.

In addition to having a low tensile load (easier to stretch), it is also important for the film to remain in place even when stretched over very dense features (light features). If sufficient residual (final) load is left, the PSA may not be able to hold the film in place over time and expose the underlying lacquer, which is considered a failure mode. To reduce the amount of residual loading, PVC film manufacturers recommend applying some heat to the film with a heat gun or similar tool after the film is fully installed. By relieving the residual load with heat, the PSA is better able to hold the film in the desired position and prevent failure. The residual load can be measured as follows: the film was stretched to a fixed strain (deformation) in a tensile tester, held at that strain for a few minutes to see how much the load was reduced, and then heated while still holding the strain to see how much the load was further reduced. At the end of heating, the residual load should be low.

The Pressure Sensitive Adhesive (PSA) layer used to adhere PVC films to vehicles is a patterned PSA that includes interconnecting air channels, textures and/or other non-tacky features to allow air to escape and optionally the film can be repositioned during installation. During the leveling process, air may escape via the air channels to prevent air bubbles from forming or to assist in the evacuation of air from air bubbles that may form during installation. The films of the present invention thus comprise a patterned PSA. Due to the air channels provided in the patterned PSA, dry mounting is possible while removing any air bubbles that may form during the mounting process. These air channels are typically formed by coating PSA onto a patterned or textured release material.

Unlike PVC automotive refinish films that are opaque with pigments and other additives, TPU protective films are generally optically clear, and thus do not use PSA systems with air channels and/or intentionally textured surfaces to achieve air evacuation; such textures and air channels are visible from the top of the film and are aesthetically unattractive. In contrast, TPU protective films use smooth and uniform PSA to achieve air evacuation and prevent entrapment of air bubbles under the film; applying a water-based slip solution or gel to the PSA and vehicle; a squeegee is used to remove air and water during installation. The initial tackiness is limited to some extent due to the use of slip solutions and high strains are generally avoided when mounting the film on complex surfaces. In addition, TPU protective films are often precut into shapes similar to vehicle body panels using a plotter and embossed cuts are made in the patterned TPU protective film to prevent bunching of the film and to avoid the need for high strain during installation. While these relief cuts are acceptable for transparent films because they are not very noticeable, they are undesirable for opaque or decorative ARWs because the underlying surface may be visibly exposed near the relief cuts after installation (e.g., white paint covered by a black film exposes white paint areas near the relief cuts).

The present invention provides a desirable combination of film properties made from polymer blends useful as ARW films for end use applications. In one aspect, the present invention has improved load attenuation under rock impact conditions, as compared to PVC ARW films, while having improved stretchability during installation. In another aspect, the present invention has improved elastic recovery and permanent set behavior compared to TPU protective films, as shown by the elastic recovery and 50% relaxation test results. In a further aspect, the present invention exhibits an improvement in residual stress after heating compared to PVC films and TPU protective films as demonstrated by 25% thermal stress relaxation test results. Finally, in one aspect, the compositions of the present invention may be halogen-free.

Films of the present invention, which may contain various modifiers such as pigments, flakes and other particles, are useful as automotive refinish films. To apply the film, the PSA is exposed by removing the silicone coated release liner and "fixing" certain locations of the film to the vehicle, and the installer uses their hands, gloved hands, squeegees or other tools to planarize the film to conform it to the vehicle body and wrap around the edges of the panel to hide the underlying color.

The application may be aided by heating the film and a post-application heat treatment is advantageously employed to secure the film in place, reduce tension and prevent post-application separation.

Typically, the installer adheres one area of the film near the middle of the automobile surface, grasps another portion of the film with his hand, and then presses (scrapes) the film onto the remaining automobile surface, stretching the film as it passes over the contours in the surface to help remove the air underneath. Alternatively, an automated process may be used to achieve the same result. The film may be further stretched during application of the film to minimize or eliminate bunching and wrinkling, or to provide the film with a surface area that is greater than it would be in an unstretched state. In performing stretching, it is important to stretch as uniformly as possible, especially at the panel edges where separation may occur and where bending may inherently result in uneven tension in the film. Given that these films are typically manually stretched, there is an upper limit to the force that an installer can withstand in order to stretch the film. The force required to stretch the film can be readily measured using standard tensile tests. In such experiments, the film was stretched at a constant deformation rate and the load was recorded with deformation. Such deformation can be easily converted into a strain value. The higher the load (normalized to the load per inch width) at a given strain value, the more difficult the stretching. Stretchability depends on the composition and thickness of the film.

It is also important for the film of the present invention to not rebound rapidly and recover its original length too quickly after stretching. This makes it easier for an installer to manipulate (position) the film around complex corners and shapes before pressing the film to adhere it to a surface. The property that controls the workability of the film is its elastic recovery, which can be measured as residual strain. Elastic recovery is defined as the residual strain on the film some time after load release. Preferably, the films of the present invention have at least some residual strain, which may be referred to as initial strain, up to one minute after load release. In this regard, high elastic materials with low residual strain levels (i.e., fast "rebound" rates) at 1 minute, such as some TPU's commonly used in PPF films, are undesirable, although they are superior to PVC films in terms of stretchability and rock resistance. In any event, it is desirable that any strain on the film eventually returns to zero, for example 24 hours after stretching.

The films of the present invention have a tensile stress at 5% strain of greater than about 20psi, or greater than 100psi, or greater than 200psi when tested by the D412 tensile test. Alternatively, the tensile stress at 5% strain may be no greater than about 700psi, or no greater than 500psi, or no greater than 300psi. Alternatively, the tensile stress at 5% strain may be about 20psi to about 700psi, or 20psi to 500psi, or 20psi to 300psi, or 20psi to 100psi, or 100psi to 700psi, or 100psi to 500psi, or 100psi to 300psi, or 200psi to 700psi, or 200psi to 500psi, or 200psi to 300psi.

The films of the present invention, when tested by the D412 tensile test and the piezoelectric impact test defined herein, have a ratio of load decay per inch of tensile stress of greater than about 70lb/lb/in, or greater than 80lb/lb/in, or greater than 90lb/lb/in, or greater than 100 lb/lb/in. Or, the ratio of load decay/tensile stress per inch may be about 70lb/lb/in to about 2500lb/lb/in, or 70lb/lb/in to 1500lb/lb/in, or 70lb/lb/in to 500lb/lb/in, or 70lb/lb/in to 400lb/lb/in, or 70lb/lb/in to 3001b/lb/in, or 801b/lb/in to 15001b/lb/in, or 80lb/lb/in to 500lb/lb/in, or 80lb/lb/in to 400lb/lb/in, or 80lb/lb/in to 3001b/lb/in, or 90lb/lb/in to 1500lb/lb/in or 90lb/lb/in to 500lb/lb/in, or 90lb/lb/in to 400lb/lb/in, or 90lb/lb/in to 300lb/lb/in, or 100lb/lb/in to 1500lb/lb/in, or 100lb/lb/in to 500lb/lb/in, or 100lb/lb/in to 400lb/lb/in, or 100lb/lb/in to 300lb/lb/in, or 100lb/lb/in to 500lb/lb/in, or 200lb/lb/in to 500lb/lb/in, or 800lb/lb/in to 2500lb/lb/in, or 900lb/lb/in to lb/in.

The films of the present invention have a 1 minute elastic recovery value of greater than about 2%, or greater than 3%, or greater than 4% when tested by the elastic recovery test defined herein. Alternatively, the composition may have a 1 minute elastic recovery value of from about 2% to about 25%, or 3% to 20%, or 4% to 15%, or up to 25%, or up to 20%, or up to 15%, or up to 10%, when tested by the elastic recovery test defined herein.

The films of the present invention may exhibit a final load of about 0.01 to about 0.30, or about 0.025 to about 0.20, or about 0.05 to about 0.175, or about 0.05 to about 0.30, or about 0.10 to about 0.25, or about 0.15 to about 0.25, or about 0.01 to about 0.07, or about 0.015 to about 0.06, or about 0.02 to about 0.05, or about 0.01 to about 0.20, or about 0.02 to about 0.15, or about 0.03 to about 0.10, or about 0.01 to about 50, or about 0.03 to about 0.025 to about 0.03 when tested at a thickness of about 0.006 inches by a 25% thermal relaxation test.

The films of the present invention may exhibit a peak load of about 0.75 to about 4.0, or about 0.85 to about 3.75, or about 1.0 to about 3.5, or about 1.5 to about 4.0, or about 1.75 to about 3.5, or about 2.0 to about 3.0, or about 0.10 to about 1.0, or about 0.25 to about 0.85, or about 0.35 to about 0.70, or about 0.75 to about 3.5, or about 1.0 to about 3.5, or about 1.25 to about 2.75, or about 0.50 to about 3.5, or about 1.0 to about 3.5, or about 1.5 to about 2.5, or about 1.5 to about 2.5, when tested at a thickness of about 0.006 inches by the 25% thermal relaxation test.

The films of the present invention may exhibit a total load reduction between peak and final loads of equal to or greater than about 90%, or equal to or greater than about 92%, or equal to or greater than 94%, or equal to or greater than about 95%, or equal to or greater than 99% when tested at a thickness of about 0.006 inch by the 25% thermal relaxation test defined herein.

In another aspect, the films of the present invention may exhibit a load under an initial relaxation of about 0.2 to about 1.5, or about 0.5 to about 1.25, or about 0.75 to 1.0, or about 0.75 to 3.0, or about 1.0 to 2.5, or about 1.15 to 2.0, or about 0.005 to 0.5, or about 0.10 to 0.40, or about 0.15 to about 0.3, or about 0.2 to about 1.5, or about 0.35 to about 1-25, or about 0.4 to about 1.0, or about 0.25 to about 2.0, or about 0.50 to about 1.5, or about 0.75 to about 1.0 when tested at a thickness of about 0.006 inches by the 25% thermal relaxation test defined herein.

In another aspect, the films of the present invention may exhibit a load of about 1.5 to about 4.5 lbf, or 2.5 to 5.0 lbf, or 3.0 to 4.5 lbf, 2.5 to 5.0 lbf, or about 2.75 to about 4.75 lbf, or about 3.0 to about 4.25 lbf, or about 0.4 to about 3.0 lbf, or about 0.50 to about 2.75 lbf, or about 0.6 to about 2.5 lbf, or about 1.5 to about 5.0 lbf, about 1.75 to about 4.0 lbf, or about 2.0 to about 3.5 lbf, or about 1.0 to about 4.5 lbf, or about 2.0 to about 3.5 lbf, or about 3.0 to about 4.5 lbf when tested according to the 50% relaxation test defined herein.

In a further aspect, the films of the present invention may exhibit a permanent set of about 25% to about 50%, or about 35% to about 50%, or about 40% to about 50%, when tested according to the 50% relaxation test.

We have found that certain compositional ranges comprising aliphatic Thermoplastic Polyurethanes (TPU), optionally prepared as a blend of different TPU's or a blend of one or more TPU's with other elastomeric polymers, can be extruded into films that exhibit better paint protection characteristics than PVC films but have less elastic rebound than TPU films, and thus are easier to install. In one aspect, the TPU comprises polycaprolactone diol. Useful optional elastomeric blend polymers may include, but are not limited to, aliphatic polycaprolactone thermoplastic polyurethane, aliphatic polyether thermoplastic polyurethane, ethylene Vinyl Acetate (EVA) and poly (cyclohexylenedimethylene cyclohexanedicarboxylate), glycol and acid comonomer (PCCE), polyvinyl chloride, thermoplastic polyamide, thermoplastic polyolefin elastomer, thermoplastic styrene block copolymer, thermoplastic aromatic copolyester ether elastomer, polyvinyl acetal such as polyvinyl butyral, or other thermoplastic polymers. In one aspect, the composition may comprise an aliphatic TPU containing a polycaprolactone diol blended with a polyvinyl acetal polymer, optionally with up to 5% additional plasticizers. When blended with a polyvinyl acetal polymer, the thermoplastic polyurethane polymer (TPU) may be present in the polymer blend in an amount of about 30 to about 99 weight percent, or about 65 to about 98 weight percent, or about 70 to about 97 weight percent, or about 75 to about 95 weight percent, or as defined elsewhere herein. In one aspect, the polyvinyl acetal polymer is polyvinyl butyral. In another aspect, the composition comprises an aliphatic TPU containing polycaprolactone diol blended with PCCE. When blended with PCCE, the thermoplastic polyurethane polymer (TPU) is typically present in the polymer blend in an amount of about 65 to about 98 weight percent, or about 70 to about 97 weight percent, or about 75 to about 95 weight percent. In another aspect, the composition or blend may be visually transparent.

The present invention relates to compositions and films comprising aliphatic thermoplastic polyurethanes or TPU. It will be appreciated by those skilled in the art that the desired properties of the TPU as described herein may be obtained by blending together thermoplastic polyurethanes of different properties, or may be the product of a single reaction. When polymers are described herein, it is therefore to be understood that the polymers may be the product of a single reaction, or may be a blend of polymers selected to impart desired properties to the blend.

TPU's can be divided into three chemical classes: polyester groups, polyether groups and polycaprolactone groups are generally referenced as polyols that react with diisocyanates and chain extenders to form polyurethanes. According to the present invention, the term "polyol" includes "polymeric glycol". Polyester TPU is generally compatible with PVC and other polar plastics and provides excellent abrasion resistance, provides a good balance of physical properties and is useful in polymer blends. Polyether-based TPUs provide low temperature flexibility and good abrasion and tear resistance. They also have good hydrolytic stability. Caprolactone TPUs have the inherent toughness and resistance of polyester-based TPUs and good low temperature properties and hydrolytic stability.

The structure of the TPU consists of hard segments and soft segments. The hard segment consists of a combination of isocyanate and chain extender, while the soft segment is a polyester, polyether or polycaprolactone polyol. The soft segment percent is the ratio of the molar mass of the polyol divided by the total molar mass of soft segment plus hard segment. In one aspect, the soft segment in the present invention may constitute from about 35 to about 60 wt.%, or from about 40 to 60 wt.%, or from about 45 to 60 wt.%, or from about 50 to 60 wt.%, or from about 40 to about 55 wt.%, or from about 40 to 50, or from about 45 to about 55 wt.% of the thermoplastic polyurethane polymer.

The TPUs can also be subdivided into aromatic and aliphatic TPUs, in which case reference is made to the diisocyanates used. Aromatic TPUs based on isocyanates such as Toluene Diisocyanate (TDI) and diphenylmethane diisocyanate (MDI) are the majority of TPU's and are used when strength, flexibility and toughness are desired. However, they are generally less weather resistant. Aliphatic TPUs based on isocyanates such as 4,4' -dicyclohexylmethane diisocyanate (H12 MDI), hexamethylene Diisocyanate (HDI) and isophorone diisocyanate (IPDI) are light stable and provide excellent transparency. They are commonly used in automotive interior and exterior applications and can be used to bond safety glass together. We have found that aliphatic polycaprolactone-based TPUs provide a good balance of weatherability, low temperature flexibility and impact resistance required for many automotive exterior applications and are particularly useful in accordance with the present invention.

In a particular aspect, the thermoplastic polyurethane useful according to the present invention can be an aliphatic polycaprolactone-based thermoplastic polyurethane comprised of a polycaprolactone-based polyol reacted with an aliphatic diisocyanate and optionally a chain extender. In this regard, the aliphatic diisocyanate may be selected from, for example, 4' -dicyclohexylmethane diisocyanate (also known as H12 MDI or HMDI), hexamethylene diisocyanate (also known as HDI or 1, 6-hexane diisocyanate), and isophorone diisocyanate (also known as 5-isocyanato-1- (isocyanatomethyl) -1, 3-trimethylcyclohexane or IPDI). In one aspect, the aliphatic diisocyanate comprises at least 80 mole% of one or more of 4,4' -dicyclohexylmethane diisocyanate, hexamethylene diisocyanate, or isophorone diisocyanate. In one aspect, the chain extender comprises a diol having 2 to 10 carbon atoms. In one aspect, the chain extender comprises 1, 4-butanediol. In one aspect, the polycaprolactone-based polyol is composed of caprolactone units and may be initiated by a diol such as ethylene glycol, diethylene glycol, hexylene glycol, neopentyl glycol, or butanediol. In a preferred aspect, the thermoplastic polyurethane comprises residues of HMDI, 1, 4-butanediol, and caprolactone.

The polycaprolactone-based polyols used to form the thermoplastic polyurethane of the present invention may have a molecular weight of, for example, from about 400 to about 4000, or 600 to 2500, or 800 to 2000, or about 750 to about 2,000, or about 900 to about 1,500. In one aspect, the polycaprolactone-based polyol used to form the thermoplastic polyurethane of the present invention is initiated by one or more of neopentyl glycol, 1, 4-butanediol, or diethylene glycol. In some aspects, the thermoplastic polyurethane of the present invention may comprise a small amount of an aromatic diisocyanate, such as diphenylmethane diisocyanate (MDI) or Toluene Diisocyanate (TDI), for example, in an amount of no greater than 20 mole%, or no greater than 15 mole%, or no greater than 10 mole%.

In one aspect, aliphatic polycaprolactone-based thermoplastic polyurethanes useful according to the present invention have a Tg of about-30 ℃ to about 60 ℃, or about-20 ℃ to about 40 ℃, as measured by differential scanning calorimetry or dynamic mechanical thermal analysis. In another aspect, aliphatic polycaprolactone-based thermoplastic polyurethanes useful according to the present invention have a weight average molecular weight of 50,000 daltons to 400,000 daltons, or about 60,000 daltons to about 350,000 daltons, or about 100,000 daltons to about 300,000 daltons, as measured by Gel Permeation Chromatography (GPC).

Other properties of aliphatic polycaprolactone-based thermoplastic polyurethanes include inherent toughness and resistance of polyester-based TPU, as well as good low temperature properties, good weatherability and light resistance, and hydrolytic stability.

In another particular aspect, the thermoplastic polyurethane useful according to the present invention may be an aliphatic polyether-based thermoplastic polyurethane composed of a polyether polyol reacted with an aliphatic diisocyanate and optionally a chain extender. In this regard, the aliphatic diisocyanate may be selected from, for example, 4' -dicyclohexylmethane diisocyanate (also known as H12MDI or HMDI), hexamethylene diisocyanate (also known as HDI or 1, 6-hexane diisocyanate), and isophorone diisocyanate (also known as 5-isocyanato-1- (isocyanatomethyl) -1, 3-trimethylcyclohexane or IPDI). In one aspect, the aliphatic diisocyanate comprises at least 80 mole% of one or more of 4,4' -dicyclohexylmethane diisocyanate, hexamethylene diisocyanate, or isophorone diisocyanate. In one aspect, the chain extender comprises a diol having 2 to 10 carbon atoms. In one aspect, the chain extender comprises 1, 4-butanediol. In one aspect, the ether-based polyol consists of polypropylene glycol (PPG) or polytetramethylene ether glycol (PTMEG). In a preferred aspect, the thermoplastic polyurethane comprises residues of HMDI, 1, 4-butanediol, and polytetramethylene ether glycol.

The polyether polyols used to form the thermoplastic polyurethane of the present invention may have a molecular weight of, for example, from about 200 to about 5,000, from about 400 to about 4,000, or from 500 to about 2,000, or from 700 to about 1,500. In some aspects, the thermoplastic polyurethane of the present invention may comprise a small amount of an aromatic diisocyanate, such as diphenylmethane diisocyanate (MDI) or Toluene Diisocyanate (TDI), for example, in an amount of no greater than 20 mole%, or no greater than 15 mole%, or no greater than 10 mole%.

In one aspect, aliphatic polyether-based thermoplastic polyurethanes useful according to the present invention have a Tg of about-80 ℃ to about 60 ℃, or about-60 ℃ to about 40 ℃, as measured by differential scanning calorimetry or dynamic mechanical thermal analysis. In another aspect, aliphatic polyether-based thermoplastic polyurethanes useful according to the present invention have a weight average molecular weight of 50,000 daltons to 400,000 daltons, or about 60,000 daltons to about 350,000 daltons, or about 100,000 daltons to about 300,000 daltons, as measured by Gel Permeation Chromatography (GPC).

Other properties of aliphatic polyether-based thermoplastic polyurethanes include good low temperature properties, good weatherability and light resistance, and hydrolytic stability.

TPUs more generally include those disclosed and claimed in U.S. Pat. No. 10,265,932, the disclosure of which is incorporated herein by reference. They are polymers containing urethane (also known as urethane) linkages, urea linkages, or combinations thereof (i.e., in the case of poly (urethane-urea)). Thus, the polyurethanes useful according to the present invention contain at least urethane linkages and optionally urea linkages. In one aspect, the polyurethane-based layer of the present invention may be based on a polyurethane in which the backbone has at least about 80% of urethane and/or urea linkages formed during its polymerization, or at least 90% or at least 95% of urethane and/or urea linkages formed during its polymerization.

The TPU useful according to the present invention may comprise polyurethane polymers of the same or different chemistries, i.e., polymer blends. Polyurethanes generally comprise the reaction product of at least one isocyanate-reactive component, at least one isocyanate-functional component, and one or more optional components such as emulsifiers and chain extenders.

The isocyanate-reactive component typically contains at least one active hydrogen, such as amines, thiols, and polyols, particularly hydroxy-functional materials, such as polyols that provide urethane linkages when reacted with the isocyanate-functional component. Specific polyols of interest include polyester polyols (e.g., lactone polyols) and alkylene oxide adducts thereof (e.g., ethylene oxide; 1, 2-propylene oxide; 1, 2-butylene oxide; 2, 3-butylene oxide; methyl propylene oxide (isobutylene oxide), and epichlorohydrin), polyether polyols (e.g., polyoxyalkylene polyols such as polypropylene oxide polyols, polyethylene oxide polyols, polypropylene oxide polyethylene oxide copolymer polyols and polyoxytetramethylene polyols, polyoxycycloalkylene polyols, polythioethers, and alkylene oxide adducts thereof), polyalkylene polyols, polycarbonate polyols, mixtures thereof, and copolymers thereof. Further relevant polyols are those derived from caprolactone, referred to herein as polycaprolactone-based polyols.

In one aspect, the isocyanate-reactive component thus reacts with the isocyanate-functional component to form a polyurethane. The isocyanate functional component may comprise an isocyanate functional material or a mixture thereof. Polyisocyanates, including derivatives thereof (e.g., urea, biuret, allophanate, dimers and trimers of polyisocyanates, and mixtures thereof) (hereinafter collectively referred to as "polyisocyanates") are preferred isocyanate functional materials for the isocyanate functional component. The polyisocyanate has at least two isocyanate functional groups and provides urethane linkages upon reaction with the hydroxyl functional isocyanate reactive component. In one embodiment, the polyisocyanate useful in preparing the polyurethane is one or a combination of any aliphatic or optionally aromatic polyisocyanate used in preparing the polyurethane.

The isocyanate is typically a diisocyanate and includes aromatic diisocyanates, aromatic-aliphatic diisocyanates, cycloaliphatic diisocyanates, and other compounds blocked by two isocyanate functions (e.g., the diamino ester of toluene-2, 4-diisocyanate-blocked polypropylene oxide polyol). The diisocyanates usable according to the invention thus comprise: 2, 6-toluene diisocyanate; 2, 5-toluene diisocyanate; 2, 4-toluene diisocyanate; a benzene diisocyanate; 5-chloro-2, 4-toluene diisocyanate; 1-chloromethyl-2, 4-benzenediisocyanate; xylylene diisocyanate; tetramethyl-xylylene diisocyanate; 1, 4-butane diisocyanate; 1, 6-hexane diisocyanate; 1, 12-dodecane diisocyanate; 2-methyl-1, 5-pentane diisocyanate; methylene dicyclohexyl-4, 4' -diisocyanate; 3-isocyanatomethyl-3, 5' -trimethylcyclohexyl isocyanate (isophorone diisocyanate); 2, 4-trimethylhexyl diisocyanate; cyclohexylidene-1, 4-diisocyanate; hexamethylene-1, 6-diisocyanate; tetramethylene-1, 4-diisocyanate; cyclohexane-1, 4-diisocyanate; naphthalene-1, 5-diisocyanate; diphenylmethane-4, 4' -diisocyanate; hexahydroxylylene diisocyanate; 1, 4-benzenediisocyanate; 3,3 '-dimethoxy-4, 4' -diphenyl diisocyanate; a benzene diisocyanate; isophorone diisocyanate; polymethylene polyphenyl isocyanates; 4,4' -biphenyl diisocyanate; 4-isocyanatocyclohexyl-4' -isocyanatophenyl methane; and p-isocyanatomethylphenyl isocyanate.

The aliphatic isocyanates useful according to the present invention thus comprise aliphatic groups, which may be alkyl, alkenyl, alkynyl, etc., and may be branched or straight-chain, with straight-chain being advantageous. Examples include 1, 12-dodecane diisocyanate; 2-methyl-1, 5-pentane diisocyanate; methylene dicyclohexyl-4, 4' -diisocyanate; 3-isocyanatomethyl-3, 5' -trimethylcyclohexyl isocyanate (isophorone diisocyanate); 2, 4-trimethylhexyl diisocyanate; cyclohexylidene-1, 4-diisocyanate; hexamethylene-1, 6-diisocyanate; tetramethylene-1, 4-diisocyanate; cyclohexane-1, 4-diisocyanate; trans 1, 4-bis (isocyanatomethyl) cyclohexane (also known as 1,4-H6 XDI); and isophorone diisocyanate.

One or more chain extenders may also be used to prepare the TPU of this invention, or the TPU/copolyester ether blends of this invention. For example, such chain extenders may be any one or combination of aliphatic polyols, aliphatic polyamines, or aromatic polyamines used in the preparation of polyurethanes. Chain extenders useful according to the present invention thus include the following: 1, 4-butanediol; propylene glycol; ethylene glycol; 1, 6-hexanediol; glycerol; trimethylolpropane; pentaerythritol; 1, 4-cyclohexanedimethanol; and phenyl diethanolamine. Also noted are diols such as hydroquinone bis (beta-hydroxyethyl) ether; tetrachlorohydroquinone-1, 4-bis (beta-hydroxyethyl) ether; and tetrachlorohydroquinone-1, 4-bis (beta-hydroxyethyl) sulfide, even if containing an aromatic ring, are considered aliphatic polyols for the purposes of the present invention. Aliphatic diols of 2 to 10 carbon atoms are preferred. Particularly preferred is 1, 4-butanediol.

The polymer blends of the present invention may optionally comprise a poly (vinyl acetal) resin, such as polyvinyl butyral. Poly (vinyl acetal) resins can be prepared by acetalizing poly (vinyl alcohol) with one or more aldehydes in the presence of a catalyst according to known methods, such as those described in U.S. Pat. Nos. 2,282,057 and 2,282,026 and Wade, B.2016, vinyl Acetal Polymer, encyclopedia of Polymer Science and Technology,1-22 (in-line, copyright 2016John Wiley&Sons,Inc.).

Poly (vinyl acetal) resins generally have residual hydroxyl content, ester content, and acetal content. As used herein, residual hydroxyl content (calculated as PVOH) refers to the weight percent of hydroxyl bearing moieties left on the polymer chain. For example, poly (vinyl acetals) can be made by hydrolyzing poly (vinyl acetate) to PVOH, and then reacting the PVOH with an aldehyde, such as butyraldehyde, propionaldehyde, etc., desirably with butyraldehyde to make a polymer having repeating vinyl butyral units. In the hydrolysis of poly (vinyl acetate), not all pendant acetate groups are typically converted to hydroxyl groups. For example, reaction with butyraldehyde typically does not convert all of the hydroxyl groups on PVOH to acetal groups. Thus, in any finished polyvinyl butyral there are typically residual ester groups such as acetate groups (as vinyl acetate groups) and residual hydroxyl groups (as vinyl hydroxyl groups) as pendant groups on the polymer chain, and acetal (e.g., butyral) groups (as vinyl acetal groups). As used herein, residual hydroxyl content is measured on a weight percent basis according to ASTM 1396.

In various embodiments, the poly (vinyl acetal) resin can comprise a polyvinyl butyral resin, which is also interchangeably referred to herein as "PVB. An example of a polyvinyl butyral structure is used to further illustrate how the weight percentages are based on the partial units to which the relevant side groups are bonded:

taking the above structure of the polyvinyl butyral, the butyral or acetal content is based on the weight percent of units a in the polymer, the OH content is based on the weight percent of units B (polyvinyl OH moieties or PVOH) in the polymer, and the acetate or ester content is based on the weight percent of units C in the polymer.

The hydroxyl content of the poly (vinyl acetal) resin is not particularly limited, but suitable amounts can be at least 6, at least 8, at least 10, at least 11, at least 12, at least 13, at least 14, at least 15, at least 16, or at least 17 and in each case up to 50 wt.% or more of PVOH. In some embodiments, the poly (vinyl acetal) can have a residual hydroxyl content of less than 15 wt%, or less than 14, less than 13, less than 12, less than 11, less than 10, less than 9, or less than 8 wt%. In general, poly (vinyl acetal) resins with lower weight percentages of hydroxyl groups have the ability to absorb more plasticizer and more efficiently absorb plasticizer. In contrast, poly (vinyl acetal) resins having a higher weight percent of hydroxyl groups generally have a higher refractive index.

The poly (vinyl acetal) resin may also contain 20 wt.% or less, 17 wt.% or less, 15 wt.% or less, 13 wt.% or less, 11 wt.% or less, 9 wt.% or less, 7 wt.% or less, 5 wt.% or less, or 4 wt.% or less of residual ester groups calculated as polyvinyl esters, e.g., acetates, with the balance being acetals, e.g., butyraldehyde acetals, but optionally including minor amounts of other acetal groups, e.g., 2-ethylhexanal groups (see U.S. Pat. No. 5,137,954). As measured for residual hydroxyl groups, the weight percent of residual ester groups (i.e., residual acetate content) is based on the portion of the polymer backbone to which acetate groups (including acetate pendant groups) are attached.

The poly (vinyl acetal) resins used in the present invention can also have an acetal content of at least 50, at least 55, at least 60, at least 65, at least 70, at least 75, at least 80, at least 85, or at least 90 weight percent or greater. Additionally or alternatively, the acetal content may be at most 94, at most 93, at most 92, at most 91, at most 90, at most 89, at most 88, at most 86, at most 85, at most 84, at most 83, at most 82, at most 80, at most 78, at most 77, at most 75, at most 70, or at most 65 weight percent.

The acetal groups in the poly (vinyl acetal) resin can comprise, for example, vinyl propynyl groups or vinyl butyral groups. In one or more embodiments, the acetal groups comprise vinyl butyral groups. In some embodiments, the poly (vinyl acetal) resin can comprise the residues of any aldehyde, and in some embodiments can comprise the residues of at least one C4 to C8 aldehyde. Examples of suitable C4 to C8 aldehydes may include, for example, n-butyraldehyde, isobutyraldehyde, 2-methylpentanal, n-hexanal, 2-ethylhexanal, n-octanal, and combinations thereof. The one or more poly (vinyl acetal) resins used in the layers and interlayers described herein can comprise at least 20, at least 30, at least 40, at least 50, at least 60, or at least 70 weight percent or more of the residues of at least one C4 to C8 aldehyde based on the total weight of the aldehyde residues of the resin. Alternatively or additionally, the poly (vinyl acetal) resin can comprise no more than 99, no more than 90, no more than 85, no more than 80, no more than 75, no more than 70, or no more than 65 weight percent of at least one C4 to C8 aldehyde. The C4 to C8 aldehydes may be selected from the group listed above, or they may be selected from n-butyraldehyde, isobutyraldehyde, 2-ethylhexanal, and combinations thereof.

The weight average molecular weight of the poly (vinyl acetal) resin is not particularly limited. The poly (vinyl acetal) resin can have a weight average molecular weight (Mw) of at least 20,000, at least 30,000, at least 40,000, at least 50,000, at least 60,000, or at least 70,000, with no particular upper limit, although in practice up to 300,000 daltons is suitable, although in some cases higher molecular weights may be used. Molecular weight was measured by Size Exclusion Chromatography (SEC) using small angle laser light scattering (SEC/LALLS) or UV/differential refractometer detectors in tetrahydrofuran. Calibration of the chromatograph was performed using polystyrene standards. As used herein, the term "molecular weight" refers to weight average molecular weight (Mw).

In an important aspect, the polymer blend of the present invention further comprises a polyvinyl acetal, especially polyvinyl butyral (PVB). PVB is a clear, colorless, amorphous thermoplastic obtained by the condensation reaction of polyvinyl alcohol and butyraldehyde. The resins are distinguished by their excellent flexibility, film formation and good adhesion properties and outstanding UV resistance. The nature of PVB, such as its solubility in solvents and its compatibility with binders and plasticizers, depends on the degree of acetalization and polymerization. An increase in the number of butyral groups in the polymer generally improves the water resistance of the PVB film. PVB can also be crosslinked. The crosslinking ability depends on the number of residual OH groups in the polymer which can react with the phenolic, epoxy and melamine resins and with the isocyanate. These chemical modifications produce high quality solvent resistant PVB coatings and films. One of the primary uses of PVB films is safety glass. Due to the good adhesion of PVB to glass, most of the fragments of broken glass adhere to the surface of the PVB film, thus preventing personal injury caused by large and sharp glass fragments. PVB laminated glass also provides improved sound barrier, good impact resistance, and almost 100% ultraviolet light absorption. The latter is important to prevent the fading of the interior trim due to UV exposure.

As already described, PVB resins are made by known acetalization methods by reacting polyvinyl alcohol ("PVOH") with butyraldehyde in the presence of an acid catalyst, separating, stabilizing, and drying the resin. The resins are commercially available in various forms, for example as a whole company from Solutia Inc. (Eastman Chemical Company)Resin。

As used herein, the residual hydroxyl content (calculated as% vinyl alcohol or% PVOH by weight) in PVB refers to the amount of hydroxyl groups left on the polymer chain after processing is complete. For example, PVB can be manufactured by hydrolyzing poly (vinyl acetate) to poly (vinyl alcohol) (PVOH) and then reacting the PVOH with butyraldehyde. In the process of hydrolyzing poly (vinyl acetate), not all pendant acetate groups are typically converted to hydroxyl groups. Furthermore, the reaction with butyraldehyde typically does not convert all of the hydroxyl groups to acetal groups. Thus, in any finished PVB resin, residual acetate groups (as vinyl acetate groups) and residual hydroxyl groups (as vinyl hydroxyl groups) are typically present as pendant groups on the polymer chain. As used herein, residual hydroxyl content and residual acetate content are measured on a weight percent (wt.%) basis according to ASTM D1396.

PVB resins of the present disclosure typically have a molecular weight of greater than 40,000 daltons, or less than 500,000 daltons, or from about 40,000 to about 500,000 daltons, or from about 70,000 to about 425,000 daltons, or from about 25,000 to about 300,000, or from about 30,000 to about 300,000, or from about 50,000 to about 280,000, or from about 35,000 to about 275,000, or from about 35,000 to about 250,000, or from about 40,000 to about 230,000, as measured by size exclusion chromatography using small angle laser light scattering. As used herein, the term "molecular weight" refers to weight average molecular weight.

In another aspect, the poly (vinyl butyral) can have a% PVOH value as further described herein of from about 8.5% to about 35%, or from about 8 to about 26, or from about 9 to about 25, or from about 10 to about 24, or from about 15 to about 25, or from about 17 to about 22, or from about 18 to about 21. Alternatively, the% PVOH value of the rigid poly (vinyl butyral) can be from about 15% to about 30%, or 18% to 20%, or as further described herein.

In another aspect, the poly (vinyl butyral) can have a residual acetate content of from about 0% to about 18% as further described herein. Alternatively, the residual acetate content of the rigid poly (vinyl butyral) can be less than 10%, or less than 5%, or less than 2%, or less than 1%, or as further described herein.

The polymer blends of the present invention may optionally comprise EVA. Ethylene Vinyl Acetate (EVA), also known as poly (ethylene vinyl acetate) (PEVA), is a copolymer of ethylene and vinyl acetate. The weight% of vinyl acetate is typically from 10 to 40% variable, the remainder being ethylene. EVA copolymers based on low proportions VA (about up to 4%) may be referred to as vinyl acetate modified polyethylenes. Which is a copolymer and is processed as a thermoplastic material. It has some of the properties of low density polyethylene but increases gloss (useful for films), softness and flexibility. The material is generally considered non-toxic. EVA copolymers based on a moderate proportion VA (about 4% to 30%) are known as thermoplastic ethylene-vinyl acetate copolymers and are thermoplastic elastomeric materials. It is unvulcanized but has some of the properties of rubber or plasticized polyvinyl chloride, especially at the upper end of this range. Both filled and unfilled EVA materials have good low temperature properties and are tough. Materials with about 11% va were used as hot melt adhesives. EVA copolymers based on a high proportion VA (greater than 60%) are known as ethylene-vinyl acetate rubbers. EVA is an elastomeric polymer that produces a "rubber-like" material in terms of softness and flexibility. The material has good transparency and glossiness, low-temperature toughness, stress cracking resistance, hot melt adhesive waterproof property and ultraviolet radiation resistance. EVA has a unique vinegar-like odor and can compete with rubber and vinyl polymer products in many electrical applications.

The polymer blends of the present invention may optionally comprise a polymer plasticizer. The polymeric plasticizers useful in the present invention are polymers formed by polymerization of diols with one or more of adipic acid, phthalic acid, and sebacic acid, triethyl citrate, acetyl triethyl citrate, tri-n-butyl citrate, acetyl tri-n-butyl citrate, benzoates obtained by reaction of benzoic acid and linear/branched alkyl residues in the range of C7-C12, dibenzoates of C2-C8 linear/branched diols/diols (glycols/diols). In a specific embodiment, the polymeric plasticizer is a polymeric adipate plasticizer (polymeric adipate plasticizer). Useful plasticizers are provided under the trade name ADMEX by Eastman Chemical Company. In one embodiment, the plasticizer is present in the polymer blend in an amount of about 1% to about 5%.

The term "molecular weight" as used herein refers to weight average molecular weight (Mw). Plasticizers in the present disclosure typically have a molecular weight range of 500 to 70,000 daltons or 750 to 10,000 daltons or 1,000 to 7,500 daltons as measured by gel permeation chromatography. Molecular weight was measured by gel permeation chromatography according to ASTM method D5296-11 using an Agilent series 1200 liquid chromatography system comprising a degasser, isocratic pump, autosampler, column oven and refractive index detector. Analysis was performed using an Agilent 5 μm PLgel, guard+mixed C+Oligopore column at 30℃at a flow rate of 1.0ml/min with a sample injection volume of 25. Mu.l. The sample solution consisted of 25mg of sample in 10ml of tetrahydrofuran+10. Mu.l of toluene flow marker. Monodisperse polystyrene standards were used to determine polystyrene equivalent molecular weights.

The polymer blends of the present invention further comprise a thermoplastic copolyester ether elastomer. Thermoplastic copolyester ether elastomers have high flexibility, very high transparency, excellent toughness and puncture resistance, excellent low temperature strength, and excellent flex crack & creep resistance without plasticizers. In one embodiment, the thermoplastic copolyester ether elastomer is poly (cyclohexanedicarboxylic acid cyclohexylenedimethylene ester) (PCCE) made by the reaction of cyclohexanedicarboxylic acid dimethyl ester with cyclohexanedimethanol and polytetramethylene glycol.

The invention thus relates to the use of a blend further comprising a thermoplastic copolyester ether, which is an elastomer, in particular as a high molecular weight semi-crystalline thermoplastic copolyester ether, which is manufactured by reaction of dimethyl cyclohexanedicarboxylate with cyclohexanedimethanol and polytetramethylene glycol. The copolyester ethers useful according to the present invention have high flexibility, very high transparency, excellent toughness and puncture resistance, excellent low temperature strength, and excellent flex resistance, crack resistance, and creep resistance without plasticizers.

Copolyester ethers useful in accordance with the present invention include those disclosed in U.S. Pat. nos. 4,349,469 and 4,939,009, the disclosures of which are incorporated herein by reference. The copolyester ethers useful according to the present invention are tough, flexible materials that can be extruded into transparent sheets. They include copolyester ethers based on 1, 4-cyclohexanedicarboxylic acid or an ester thereof, 1, 4-cyclohexanedimethanol, and poly (oxytetramethylene) glycol (also known as polytetramethylene ether glycol). Copolyester ethers useful according to the present invention include those commercially available as ECDEL from Eastman Chemical Company, kingsport, TN.

In one aspect, the copolyester ether may have an inherent viscosity (ih.v.) of, for example, about 0.8 to 1.5 and repeat units from: (1) A dicarboxylic acid component comprising 1, 4-cyclohexanedicarboxylic acid or an ester thereof, typically having a trans isomer content of at least 70%, or at least 80%, or at least 85%; (2) A glycol component comprising, for example, (a) about 95 to about 65 mole% 1, 4-cyclohexanedimethanol, and (b) about 5 to about 50 mole% poly (oxytetramethylene) glycol, or 10 to 40 mole%, or 15 to 35 mole%, having a molecular weight, for example, of about 500 to about 1200, or 900 to 1,100, in both cases a weight average molecular weight.

Alternatively, the copolyester ether may have an inherent viscosity (IhV) of, for example, about 0.85 to about 1.4, or 0.9 to 1.3, or 0.95 to 1.2. As used herein, ihV is determined by dissolving a polymer sample in a solvent, measuring the flow rate of the solution through a capillary, and then calculating IhV based on the flow rate. Specifically, ASTM D4603-18,Standard Test Method for Determining Inherent Viscosity of Poly (Ethylene Terephthalate) (PET) by Glass Capillary Viscometer can be used to determine IhV. In a further aspect, the Tg of the polyester ether may have a glass transition temperature (Tg) of about-70 ℃ to about 50 ℃, or about-50 ℃ to 0 ℃ as measured according to ASTM D3418-15 and discussed further below.

In addition to 1, 4-cyclohexanedimethanol, other typical aliphatic or cycloaliphatic diols having 2 to 10 carbon atoms that may be used to form the copolyester ether include, for example, ethylene glycol, diethylene glycol, triethylene glycol, tetraethylene glycol, pentaethylene glycol, 1, 2-propanediol, 1, 4-propanediol, dipropylene glycol, 1, 2-butanediol, 1, 3-butanediol, 1, 4-butanediol, 1, 5-pentanediol, 1, 6-hexanediol, ethylene glycol, propylene glycol, butylene glycol, ethylene glycol, propylene glycol, butylene glycol, propylene glycol, butylene glycol may be propylene glycol 1, 2-cyclohexanedimethanol, 1, 3-cyclohexanedimethanol, 2-dimethyl-1, 3-propanediol (neopentyl glycol), 2-ethyl-2-isobutyl-1, 3-propanediol, 2-methyl-1, 3-propanediol, 2-butyl-2-ethyl-1, 3-propanediol, 2, 4-trimethyl-1, 3-pentanediol, 2, 4-tetramethyl-1, 3-cyclobutanediol, 2, 4-tetramethyl-1, 6-hexanediol, 1, 10-decanediol, 1, 4-benzenedimethanol, hydroxypivalyl hydroxypivalate, and combinations thereof. Although small amounts of aromatic diols may be used, this may not be preferred.

In addition to 1, 4-cyclohexanedicarboxylic acid, other aliphatic, cycloaliphatic, or aromatic diacids or dianhydrides having 2 to 10 carbon atoms that may be used to form the copolyester ether include those such as adipic acid, maleic anhydride, maleic acid, fumaric acid, itaconic anhydride, itaconic acid, citraconic anhydride, citraconic acid, dodecanedioic acid, succinic anhydride, glutaric acid, sebacic acid, azelaic acid, terephthalic acid, isophthalic acid, stilbenedicarboxylic acid, diphenic acid, hexahydrophthalic anhydride (HHPA), tetrahydrophthalic anhydride, tetrachlorophthalic anhydride, 5-norbornene-2, 3-dicarboxylic acid, 2, 3-norbornanedicarboxylic anhydride, cyclohexanedicarboxylic acid dimethyl ester (DMCD), and combinations thereof. Aliphatic acids or anhydrides are preferred.

In addition to polytetramethylene ether glycol, other useful polyether polyols having 2 to 4 carbon atoms between ether units include polyethylene glycol ether (polyethylene ether glycol) and polypropylene glycol ether (polypropylene ether glycol) and combinations thereof. According to the present invention, the term "polyol" includes "polymeric glycol". Useful commercially available polyether polyols include Carbowax resins, pluronics resins, and Niax resins. Polyether polyols useful in accordance with the present invention include those that can be generally characterized as polyalkylene oxides and can have molecular weights of, for example, from about 300 to about 10,000 or 500 to 2000.

The copolyester ether may further comprise, for example, up to about 1.5 mole%, based on the acid or glycol component, of a polyacid or polyol branching agent having at least three-COOH or-OH functional groups and 3 to 60 carbon atoms. Many esters of such acids or polyols may also be used. Suitable branching agents include 1, 1-trimethylol propane, 1-trimethylol ethane, glycerol, pentaerythritol, erythritol, threitol, dipentaerythritol, sorbitol, phenyl dianhydride, trimellitic acid or anhydride, trimellitic acid and trimer acid.

It should be understood that the total acid reactant should be 100% and the total glycol reactant should be 100 mole%. Although the acid reactant is said to contain 1, 4-cyclohexanedicarboxylic acid, if the branching agent is a polyacid or anhydride, it is calculated as part of 100 mole% acid. Likewise, the diol reactants are said to comprise 1, 4-cyclohexanedimethanol and poly (oxytetramethylene) diol; if the branching agent is a polyol, it is calculated as part of 100 mole% glycol.

The trans and cis isomer content of the final copolyester ether can be controlled to give a fast setting (setup) or crystalline polymer. The cis and trans isomer content is measured by conventional methods known to those skilled in the art. See, for example, U.S. patent 4,349,469.

Particularly suitable copolyester ethers useful according to the invention are those based on 1, 4-cyclohexanedicarboxylic acid, 1, 4-cyclohexanedimethanol and polytetramethylene ether glycol or other polyalkylene oxide glycols. In one aspect, the 1, 4-cyclohexanedicarboxylic acid is present in an amount of at least 50 mole%, or at least 60 mole%, or at least 70 mole%, or at least 75 mole%, or at least 80 mole%, or at least 85 mole%, or at least 90 mole%, or at least 95 mole%, based in each case on the total amount of dicarboxylic acids present in the copolyester ether. In another aspect, 1, 4-cyclohexanedimethanol is present in an amount of about 60 mole% to about 98 mole%, or 65 mole% to 95 mole%, or 70 mole% to 90 mole%, or 75 mole% to 85 mole%, in each case based on the total amount of diols. In another aspect, the polytetramethylene ether glycol is present in the copolyester ether in an amount of from about 2 to about 40 mole%, or 5 to 50 mole%, or 7 to 48 mole%, or 10 to 45 mole%, or 15 to 40 mole%, or 20 to 35 mole%, based in each case on the total amount of glycol present.

In a further aspect, the amount of 1, 4-cyclohexanedicarboxylic acid is from about 100 mole% to about 98 mole%, the amount of 1, 4-cyclohexanedimethanol is from about 80 mole% to about 95 mole%, the amount of polytetramethylene ether glycol is from about 5 mole% to about 20 mole%, and trimellitic anhydride can be present in an amount of 0.1 to 0.5 mole% TMA.

In a more specific aspect, the amount of 1, 4-cyclohexanedicarboxylic acid is 98 to 100 mole percent, the amount of 1, 4-cyclohexanedimethanol is 70 to 95 mole percent, the amount of polytetramethylene ether glycol is 5 to 30 mole percent, and trimellitic anhydride can be present at 0 to 0.5 mole percent.

In another more specific aspect, the amount of 1, 4-cyclohexanedicarboxylic acid is from 99 to 100 mole percent, the amount of 1, 4-cyclohexanedimethanol is from 70 to 95 mole percent, the amount of polytetramethylene ether glycol is from 5 to 30 mole percent, and trimellitic anhydride can be present in an amount of from 0 to 1 mole percent.

The copolyester ethers of the invention may comprise a phenolic antioxidant capable of reacting with the polymer intermediate. This allows the antioxidant to be chemically attached to the copolyester ether and substantially unable to be extracted from the polymer. Antioxidants useful in the present invention may contain one or more of an acid group, a hydroxyl group, or an ester group that is capable of reacting with the reagents used to prepare the copolyester ether. Phenolic antioxidants are preferably hindered and relatively nonvolatile. Examples of suitable antioxidants include hydroquinone, aromatic amine antioxidants such as 4,4' -bis (α, α -dimethylbenzyl) diphenylamine, hindered phenol antioxidants such as 2, 6-di-tert-butyl-4-methylphenol, butylated para-phenylphenol and 2- (α -methylcyclohexyl) -4, 6-dimethylphenol; bisphenols such as 2,2 '-methylenebis- (6-tert-butyl-4-methylphenol), 4' -bis (2, 6-di-tert-butylphenol), 4 '-methylenebis (6-tert-butyl-2-methylphenol), 4' -butylidenebis (6-tert-butyl-3-methylphenol), methylenebis- (2, 6-di-tert-butylphenol), 4 '-thiobis (6-tert-butyl-2-methylphenol) and 2,2' -thiobis (4-methyl-6-tert-butylphenol); triphenols, such as 1,3, 5-tris (3, 5-di-tert-butyl-4-hydroxyhydrocinnamoyl) -hexahydro-s-triazine, 1,3, 5-trimethyl-2, 4, 6-tris (3, 5-di-tert-butyl-4-hydroxybenzyl) benzene and tris (3, 5-di-tert-butyl-4-hydroxyphenyl) phosphite; and tetrakis [ methylene (3, 5-di-tert-butyl-4-hydroxyhydrocinnamate) methane ], which is available as Irganox 1010 antioxidant from Geigy Chemical Company. Preferably, the antioxidants are used in an amount of about 0.1 to about 1.0 based on the weight of the copolyester ether.

The copolyester ethers of the present invention include those characterized by their good melt strength. Polymers having melt strength are described as polymers capable of supporting themselves as they are extruded downwardly from a die in the melt. When a polymer with melt strength is extruded downward, the melt will remain together. When a polymer without melt strength is extruded downward, the melt drops rapidly and breaks. For comparison, melt strength was measured at a temperature 20℃higher than the melting peak.

Many useful applications are contemplated for forming blends of these films, such as paint protective films, automotive refinish films, graphic films (graphic films), medical fabrics, breathable textiles, smart apparel, surface protective films, touch screen films, automotive interior trim cover films, laminated glass innerlayers, tubing and hoses, tapes and profiles, seals and gaskets. This list is by no means exhaustive. Thus, the polymer blend may be melt compounded in a variety of ways to be ultimately formed into an article. In one embodiment, the film has a thickness of about 50 to about 300 microns, or about 100 to about 300, or about 125 microns to about 200 microns. In one embodiment, the film may further comprise an adhesive layer. In another embodiment, the film may further include a protective top coating, such as acrylic, polyester, polyurethane, or blends thereof, on the side of the film opposite the adhesive layer. Such top coats may contain additives such as fluoropolymers, silicon compounds, nanoparticles, and the like. Although a protective top coat may be advantageous, the presence of the top coat should not unduly affect the desired properties of the compositions and films of the present invention.

In one aspect, the polymer blend may be formed in a plastic compounding line, such as a twin screw compounding line. In this regard, the pellets were dried at about 125°f for 4 to 6 hours to remove any moisture. The pellets may then be fed into the throat of an extruder and melted at 170°f to 200°f to produce a viscous thermoplastic material. The polymer blends may be pre-blended and added as a single blend with a loss-in-weight feeder, or may be added separately with a loss-in-weight feeder. The rotation of the two screws disperses and melts the polymer blend. The mixture is then extruded through a die to produce a plurality of strands. The strands may be fed through a water trough to cool the pellets. After leaving the flume, the strands are dried and fed into a dicer to cut the strands into pellets. Alternatively, the mixture may be extruded into water through a circular flat die having a plurality of openings. The flat die has a rotary cutter that cuts the strands as they are extruded from the die to produce pellets. The continuous water stream cools the pellets and conveys them to a drying section, typically a centrifuge, to separate the pellets from the water.

In another aspect, the polymer blend may be formed in a plastic compounding line, such as a twin rotor continuous compounding mixer (e.g., a Farrell continuous mixer). In this case, the pellets may be dried at about 125°f for 4 to 6 hours to remove any moisture. The pellets were fed into the throat of a continuous mixer and melted into a homogeneous mixture at 170°f to 200°f. The output rate of the mixer is controlled by varying the area of the discharge port. The melt may be cut into "chunks" and fed into the throat of a twin roll mill or single screw extruder. In the case of feeding the melt into a twin roll mill, the melt covers one of the rolls and the strip may be fed into the throat of a single screw extruder. The mixture is then extruded through a die to produce a plurality of strands. The strands may be fed through a water trough to cool the pellets. After leaving the flume, the strands are dried and fed into a dicer to cut the strands into pellets.

Alternatively, the mixture may be extruded into water through a circular flat die having a plurality of openings. The flat die has a rotary cutter that cuts the strands as they are extruded from the die to produce pellets. The continuous water stream cools the pellets and conveys them to a drying section, typically a centrifuge, to separate the pellets from the water. In the case of feeding "blocks" into a single screw extruder, the mixture is extruded through a die to produce multiple strands. The strands may be fed through a water trough to cool the pellets. After leaving the flume, the strands are dried and fed into a dicer to cut the strands into pellets.

Alternatively, the mixture may be extruded into water through a circular flat die having a plurality of openings. The flat die has a rotary cutter that cuts the strands as they are extruded from the die to produce pellets. The continuous water stream cools the pellets and conveys them to a drying section, typically a centrifuge, to separate the pellets from the water.

In a further aspect, the polymer blend may be formed in a high intensity mixer, such as a Banbury batch mixer. In this case, the pellets may be dried at about 125°f for 4 to 6 hours to remove any moisture. The pellets are loaded into a high intensity mixer and the ram is lowered to compress the pellets into the mixing chamber. Two rotating mixer blades melt the pellets. When the desired temperature of 170°f to 200°f was reached, the door at the bottom of the mixer was opened and the mixture was fed into a two-roll mill. The strip from the twin roll mill may then be fed into a single screw extruder. The mixture is then extruded through a die to produce a plurality of strands. The strands may be fed through a water trough to cool the pellets. After leaving the flume, the strands are dried and fed into a dicer to cut the strands into pellets.

In various aspects, the present invention contemplates several different methods for making plastic articles: extrusion to produce continuous flat sheets, profiles or fibers, or injection molding to make discrete articles.

In one aspect, the present invention relates to extruding "fully compounded" pellets or polymers at a desired polymer blend concentration ratio to produce films, flat sheets, profiles or fibers. In this case, the pellets were dried at about 125°f for 4 to 6 hours to remove any moisture and then fed into a single screw extruder, twin screw extruder or conical twin screw extruder. The pellets are conveyed and compressed down the extruder barrel by one or more screws to melt the pellets and discharge the melt from the end of the extruder. The melt may be fed through a screening device to remove debris and/or through a melt pump to reduce pressure variations caused by the extruder. The melt may then be fed through a die to produce a continuous film or flat sheet, or into a profile die to produce a continuous shape.

In the case of a flat sheet die, the melt may be extruded onto a series (typically three) of metal rolls to cool the melt and provide a finish (finish) on the sheet, or for films, the melt may be "cast" onto the metal rolls or onto a continuous carrier film that acts as a release liner. The film or flat sheet is then conveyed in a continuous sheet for cooling on a series of cooling rolls. It can then be trimmed to the desired width and then wound into a roll or sheared or sawed into sheet form. The flat sheet can also be shaped mechanically into the desired shape and then cooled by spraying water, by a water bath or by blowing air over the profile. It may then be sawed or sheared to the desired length. In the case of profile dies, the die is designed to produce the desired shape of the article. After leaving the die, it can then be cooled by spraying water, by a water trough or by blowing air over the profile. It may then be sawed or sheared to the desired length. In the case of fibers, the fibers can be drawn from the extrusion die spinneret to a desired fiber diameter.

In another aspect, the present invention relates to extruding neat pellets at a desired polymer blend concentration of polymer. The pellets were dried at about 125°f for 4 to 6 hours prior to extrusion. The pellets may be dried separately or blended together after a low intensity mixer such as a ribbon blender, tumbler or conical screw blender. The pellets are then fed into a single screw extruder, twin screw extruder or conical twin screw extruder. The pellets are conveyed and compressed down the extruder barrel by one or more screws to melt the pellets and discharge the melt from the end of the extruder. The melt may be fed through a screening device to remove debris and/or through a melt pump to reduce pressure variations caused by the extruder. The melt may then be fed through a die to produce a continuous film or flat sheet, or into a profile die to produce a continuous shape.

In the case of a flat sheet die, the melt may be extruded onto a series (typically three) of metal rolls to cool the melt and provide a finish on the sheet, or for films, the melt may be "cast" onto the metal rolls or onto a continuous carrier film that acts as a release liner. The film or flat sheet is then conveyed in a continuous sheet for cooling on a series of cooling rolls. It can then be trimmed to the desired width and then wound into a roll or sheared or sawed into sheet form. The flat sheet can also be shaped mechanically into the desired shape and then cooled by spraying water, by a water bath or by blowing air over the profile. It may then be sawed or sheared to the desired length. In the case of profile dies, the die is designed to produce the desired shape of the article. After leaving the die, it can then be cooled by spraying water, by a water trough or by blowing air over the profile. It may then be sawed or sheared to the desired length. In the case of fibers, the fibers can be drawn from the extrusion die spinneret to a desired fiber diameter.

In another aspect, the present invention relates to extruding "fully compounded" pellets or polymers at a desired polymer blend ratio to produce injection molded articles. In this case, the pellets were dried at 150°f to 160°f for 4 to 6 hours to remove any moisture and then fed into a reciprocating single screw extruder. The pellets are melted by rotation and reciprocation of the screw. Once the pellets reach the desired temperature, the gate is opened at the end of the extruder and the molten plastic is pumped by a screw into a heated mold to form the desired shaped article. Once the mold is full, coolant is pumped through the mold to cool the mold and the molten plastic. Once the plastic is cured, the mold is opened and the article is removed from the mold. Typical extruder processing conditions are given below:

TABLE 1 typical extrusion conditions

Unless otherwise indicated, all numbers expressing quantities of ingredients, properties such as molecular weight, reaction conditions, and so forth, used in the specification and claims are to be understood as being modified in all instances by the term "about". Accordingly, unless indicated to the contrary, the numerical parameters set forth in the following specification and attached claims are approximations that may vary depending upon the desired properties sought to be obtained by the present invention. At the very least, each numerical parameter should at least be construed in light of the number of reported significant digits and by applying ordinary rounding techniques. Furthermore, the scope defined in the disclosure and claims is intended to expressly include the entire scope rather than just one or more endpoints. For example, a range specified as 0 to 10 is intended to disclose all integers between 0 to 10, such as 1, 2, 3, 4, etc., all fractions between 0 to 10, such as 1.5, 2.3, 4.57, 6.1113, etc., and endpoints 0 and 10.

Notwithstanding that the numerical ranges and parameters setting forth the broad scope of the invention are approximations, the numerical values set forth in the specific examples are intended to be reported precisely in accordance with the measurement methods. Any numerical value, however, inherently contains certain errors necessarily resulting from the standard deviation found in their respective testing measurements.

It is to be understood that reference to one or more process steps does not exclude the presence of additional process steps before or after the listed steps in combination or intermediate process steps between those steps explicitly stated. Furthermore, unless otherwise indicated, other aspects of the process steps, components, or information disclosed or claimed in this application are named alphabetically, numerically, etc. as a convenient means of identifying discrete activities or components, and the listed alphabetic designations may be arranged in any order.

As used herein, the singular forms "a", "an" and "the" include plural referents unless the context clearly dictates otherwise. For example, for C _n References to alcohol equivalents are intended to include various types of C _n Alcohol equivalents. Thus, unless the context clearly dictates otherwise, even if a term such as "at least one" or "at least some" is used at a location, it is not intended that other applications of "a", "an", and "the" exclude a plurality of objects. Similarly, the use of terms such as "at least some" in one location is not intended to imply that such terms are not present in other locations to mean "all" unless the context clearly dictates otherwise.

The term "and/or" as used herein when used in a list of two or more items means that any one of the listed items can be used alone or any combination of two or more of the listed items can be used. For example, if the composition is described as containing components A, B and/or C, the composition may contain a alone; only B; only C; a combination comprising a and B; a combination comprising a and C; a combination comprising B and C; or a combination of A, B and C.

The invention may be further illustrated by the following examples of embodiments thereof, but it is to be understood that these examples are intended as illustrations only and are not intended to limit the scope of the invention unless otherwise specifically indicated.

Examples

All samples were prepared by bag blending pellets of the various materials, extruding the pellet blend in an X-ploe mini-extruder and then pressing the extruded strands into a film on a Carver press. The films were tested for tensile properties, stress relaxation at 50% strain, stress relaxation at 25% strain upon application of heat to the film, stress recovery at 25% strain, and impact force attenuation. The transparency of the samples was also assessed visually.

Preparation of the samples:

samples of polymer strands were prepared using an X-plore twin screw micro extruder. Cooling water and ventilation are used. The middle zone temperature was set at 180 ℃, the extruder speed was 150RPM, the maximum force was set at 10000N, and the acceleration was set at 800RPM/min. The raw materials were weighed to a batch size of up to 8 grams and thoroughly mixed in a closed extruder for 1 minute. Strands (diameter 5 mm) were extruded and collected on a flat glass plate, which was allowed to cool to room temperature.

The polymer strands were then pressed on a Carver press. The heated platen was set to 180 ℃. The polymer is placed between two thick metal plates with a silicone film between the polymer and the metal plates. The plates were then placed between platens and preheated for 1 minute. The pressure was adjusted to a minimum and the platens were raised together and heated for 1 minute. When a metal shim is used, the load is increased. If a metal shim is used to control the thickness, the load is increased to 40,000 pounds. If shims were not used, the load was increased to 10,000 to 35,000 pounds. Depending on the rheological properties of the polymer, this resulted in a film that was 0.006 "to 0.010" thick. The cooling water was then turned on to cool the heated platen to 100 ℃, and then the water was turned off. The platen was opened, the sample was removed and cooling to room temperature was completed.

And (3) testing:

tensile Properties

The tensile properties of the films were tested according to ASTM D412-16 (re-approval of 2021) (Standard Test Methods for Vulcanized Rubber and Thermoplastic Elastomers-tensile) using test method A. Film samples were cut into dog bone specimens using ASTM die B prior to measurement. All samples were conditioned at a temperature of 73+/-2F and a relative humidity of 50+/-5% according to ASTM D-618-21 "Standard Practice for Conditioning Plastics for Testing". Testing was performed using a MTS weight 50W electromechanical testing system and programming and control was performed using TestWorks version 4.11 software. To hold the sample in the instrument, a pneumatic clamp was retrofitted to the ight 50W. Young's modulus, secant modulus, ultimate tensile strength, ultimate elongation and stress at various strain levels were measured and recorded.

50% stress relaxation

To measure peak load and permanent set at 50% strain, films were tested according to the modified version of ASTM D412-16 (re-approval of 2021) (Standard Test Methods for Vulcanized Rubber and Thermoplastic Elastomers-session) using the apparatus described above. The film samples were cut into lengths of 6 inches and widths of 0.500 inches prior to measurement. All samples were conditioned at a temperature of 73+/-2F and a relative humidity of 50+/-5% according to ASTM D-618-21 test "Standard Practice for Conditioning Plastics for Testing" and tested at a gauge length of 2 inches (initial length) extended at a speed of 20 inches/minute. Each sample was elongated to 50% strain (strain length) and this strain was maintained for 120 seconds. After 120 seconds of hold, the strain was reduced to 0% at a rate of 20 inches/minute. The length (final length) corresponding to the load value of 0 lbs was recorded. The load was measured throughout the cycle and a single cycle was performed for each sample. Duplicate samples of each sample type were tested, and the two measurements were averaged and reported. Peak load (load at 50% strain) was measured and normalized to equivalent load at 6mil (4.5 mil for vinyl film) film thickness. For example, if the measured load of the film is 2 lbs. at a thickness of 3 mils, we report a value of 4 lbs. (2 lbs. x (6 mil/3 mil) =4 lbs) in the comparative table. Using the above terms, the equation for calculating permanent set is as follows:

Permanent set = ((final length-initial length)/initial length) x 100%

25% thermal stress relaxation

Modified versions of ASTM D412 (Standard Test Methods for Vulcanized Rubber and Thermoplastic Elastomers-session) using the above apparatus were developed to determine various loads after elongation to 25% strain and retention at two different temperatures. The film samples were cut into lengths of 6 inches and widths of 0.500 inches prior to measurement. All samples were conditioned at 73+/-2F and 50+/-5% relative humidity for 40 hours according to ASTM D-618-21 "Standard Practice for Conditioning Plastics for Testing'". Each film sample was stretched to 25% strain and held at room temperature for 2 minutes. After the initial 2 minute hold, the entire gauge length of the film was heated with a heat gun as described below for 1 minute to 168+/-3°f. After heating for 1 minute, the heat was removed and the film was kept at room temperature for another 2 minutes. The load is measured throughout the run. Peak load is defined as the maximum load encountered when stretched to 25% strain. The load at initial relaxation is defined as the load measured at the end of the first 2 minutes of hold at room temperature. The final load is defined as the load measured after heating for 1 minute and then holding at room temperature for 2 minutes after removal of heat. For all non-vinyl samples, the measured load was normalized to the equivalent load at a film thickness of 6 mils (0.006 inch). For example, if the load measured on a non-vinyl film at a thickness of 3 mils is 2lbs, we report a value of 4lbs (2 lbs x (6 mil/3 mil) =4 lbs) in the comparative table. From these load values, the relaxation values are calculated as follows:

Initial relaxation = (1- (load/peak load under initial relaxation)) x 100%

Final relaxation = (1- (final load/load under initial relaxation)) x 100%

Total relaxation = (1- (final load/peak load)) x 100%

25% elastic recovery

To measure elastic recovery at 25% strain, the test specimens were cut into 4 inch by 0.5 inch strips and two lines spaced 1 inch apart were marked in the middle of each specimen. The sample was stretched to 25% in 2 seconds (tensile strain) and then held at 25% for 30 seconds and allowed to relax at room temperature. The final distance between the wires was measured again 1 minute, 5 minutes and 24 hours after stretching. The residual strain at each of these times was calculated as follows:

residual strain = ((final distance-1 inch)/1 inch) x 100%

Impact force attenuation

The impact force was measured using a piezodynamic force sensor available from PCB Piezoelctronics, model 208C05, with a compressive load ranging from 0 to 5000lbs and a sensitivity of 1mV/lb. A 1 inch diameter steel ball with a mass of 8.44gm falls from the 36 inch through the tube to strike the sensor (impact velocity of about 10 mph). The electrical signal from the impacted sensor was sent through a Model 480C02 signal conditioner (Signal Conditioner) and converted to a load value using National Instruments data acquisition card and LabView software. The impact force is first measured without a membrane placed, and then measured with the membrane placed on top of the sensor such that the membrane is between the sensor and the ball drop. The load measured with the membrane was subtracted from the load measured without the membrane to determine the amount of membrane decay load.

To determine the ratio of load decay to "stretchability," the D412 tensile stress at 5% strain was multiplied by the film thickness to determine the load/inch value. The damping load is then divided by this load/inch and added to the table. The ratio is in lb/lb/in.

Glass transition temperature data

The glass transition temperature was measured using ASTM D3418-15. The sample was heated from-50 ℃ to 150 ℃ at 20 ℃/min, cooled to-50 ℃ and then re-heated from-50 ℃ to 150 ℃ at 20 ℃/min. The glass transition temperature is determined by preliminary (i.e., first) heating on the sample for at least one month after extrusion.

Determination of the type of diol and initiator by GC/MS after hydrolysis

The sample was hydrolyzed by weighing about 0.2 g of the sample in an 8-drum vial, adding 1 ml of 5M NaOH/MeOH and 4 ml of DMSO, heating at 90℃and stirring for about 1-2 hours. The vial was cooled and 5 ml DMF and 0.3 ml H3PO4 were added. 0.3 ml of the supernatant was taken into a GC vial, 1 ml of BSA was added, and heated at 90℃for 20 minutes. Samples were analyzed on a Thermo ISQ LT GC-MS.

Determination of isocyanate type by pyrolysis GC/MS

About 100 mg of the sample was subjected to pyrolysis-GC/MS (Py-GC/MS). The sample was introduced into a 600 ℃ pyrolysis furnace for 1 minute while the precipitated pyrolysate was captured at a low temperature at the top of the GC column. The pyrolysis products (pyrolysates) were then separated by gas chromatography and detected by mass spectrometry. GC analysis was run on an Agilent model 7890A and MS analysis was run on an Agilent model 5977A, the pyrolysis unit being Frontier Labs Multi-Shot Pyrolyzer/Furnace model EGA/PY-3030D.

Polymer composition data of aliphatic polyether TPU determined by nuclear magnetic resonance

The TPU sample is solvated in CDCl3 to a TPU concentration of 20-30mg/ml for 1H-NMR. More concentrated samples (100 mg/mL) were used for 13C-NMR and 1H-13C Heteronuclear Single Quantum Coherence (HSQC) experiments. For 13C-NMR quantitative analysis, chromium acetylacetonate (0.01M) was added. Each 13C-NMR experiment has 12000 runs to obtain high quality data, which typically takes about 10 hours. 500MHz Bruker Avance I spectrometer NMR was used to characterize the hard and soft segments and determine their relative weight percent.

The heat gun was a Steinel Electronic Heat Gun Model HG2310LCD equipped with a 75mm expanding nozzle (nozzle). The long dimension of the expansion nozzle was positioned about 2 cm from and parallel to the long dimension of the film sample.

Determination of TPU molecular weight by GPC

The molecular weight and distribution of the thermoplastic polyurethane were determined by gel permeation chromatography at 30 ℃. The thermoplastic polyurethane was sufficiently dissolved in chloroform at a concentration of 2.5 mg/mL. A series of monodisperse polystyrene (mw=580 to 4,000,000) was used as a standard and refractive index RI was measured.

PVB characterization

Table 1 shows the different PVB resins used in this study. Butvar resins are commercially available from Eastman Chemical Company, kingsport, TN. Resins PVB1, PVB2, and PVB3 are variants produced for this study using the same method used to produce the commercial resins, but with different molecular weights and residual PVOH content. The% PVOH of all resins was measured according to ASTM D1396. Molecular weight is measured by Size Exclusion Chromatography (SEC) using small angle laser light scattering (SEC/LALLS) or UV/differential refractometer detectors. As used herein, the term "molecular weight" refers to weight average molecular weight (Mw). SEC analysis was performed using a Waters 2695 Alliance pump and autosampler with a Waters 410 online differential refractive index detector and a Waters 2998 PDA online UV detector (available from Waters Corporation, milford, mass.) and Dionex Chromeleon v.6.8 data acquisition software with an extension package (available from Thermo Fischer Scientific, sunnyvale, calif.). Analysis was performed with PL Gel Mixed C (5 micron) column and Mixed E (3 micron) column at a flow rate of 1.0 ml/min at a sample volume of 50 μl. Samples were prepared by dissolving 0.03 to 0.09 grams of resin in 10-15 milliliters of solvent, and then each filtered through a 0.22 micrometer PTFE filter. Calibration of the chromatogram was performed using polystyrene standards (available as PSBR250K from American Polymer Standard Corporation, mentor, ohio).

Conversion to

1lb＝454gm

1in＝25.4mm

1mil＝0.0254mm

1lb/in＝17.87gm/mm

1lb/lb/in＝25.4gm/gm/mm

1psi＝0.00689MPa

TABLE 2 list of raw materials

TABLE 3 determination of the composition of aliphatic polycaprolactone TPU by GC/MS and NMR

Hydrolysis GC/MS determines the soft segment (polyol) as caprolactone and pyrolysis GC/MS determines the isocyanate as 4,4' -methylenebis (cyclohexyl isocyanate). The chain extender was determined to be 1, 4-butanediol. The NMR measurement composition is as follows:

TABLE 4 glass transition temperature data for aliphatic polycaprolactone TPU blends

Examples	Description of formulation	Tg
			1	87A	-17.7℃
2	75％87A/25％60D	-11.9℃
			3	50％87A/50％60D	-6.7℃
4	25％87A/75％60D	5.0℃
			5	60D	11.3℃

TABLE 5 determination of the composition of aliphatic polyether TPUs by GC/MS and NMR

The soft segment (polyol) was determined by hydrolysis GC/MS to be polytetramethylene glycol (PTMG) and the isocyanate was determined by pyrolysis GC/MS to be 4,4' -methylenebis (cyclohexyl isocyanate). The chain extender was determined to be 1, 4-butanediol. Other properties are shown below.

TABLE 6 PVB Properties

PVB grade	Mw	PVOH wt%
			B-72	170 to 250K	17.5 to 20.0
B-79	50 to 80K	11.0 to 13.5
			B-90	70 to 100K	18.5 to 20.5
B-98	40 to 70K	18.0 to 20.0
			PVB1	150 to 225	18.7
PVB2	170 to 250K	18.7
			PVB3	150 to 225	24.0

Tables 7, 9, 12 and 15 above contain ASTM D412 tensile data. Examples PVC 1 to PVC 21 in table 7 are commercial PVC automotive wrap films. Examples 47 to 50 in table 15 are blends of TPU 87A with Ecdel PCCE. Comparing the stress values at 5% strain, it can be seen that the TPU/PCCE blend requires much less stress than the commercial PVC film to pull to 5% strain. These TPU/PCCE films are much easier to install on automobiles and cause less fatigue to the installer because less force is required than PVC films.

Tables 8, 10, 13 and 16 above contain the damping load values from the impact force damping test. The tensile load value per inch width at 5% strain was calculated from the D412 stress value at 5% strain by multiplying the stress at 5% strain by the sample thickness used in the impact force attenuation test. The ratio of the decay load to the load per inch at 5% strain was then calculated. Examples PVC 1 to PVC 21 in table 8 are commercial PVC automotive wrap films. Examples 47 to 50 in table 16 are blends of TPU 87A with Ecdel PCCE. Comparing the values of this ratio, it can be seen that the TPU/PCCE blend provides much greater load attenuation (i.e., rock resistance) and much less stress to pull to 5% strain than commercial PVC films. These TPU/PCCE films are therefore preferred over PVC films from both a rock resistance and installation point of view.

Tables 8, 10, 13 and 16 above also contain the residual load values after the time of the 25% elastic recovery test. Examples 47 to 50 in table 16 are blends of TPU 87A with Ecdel PCCE. Comparison of examples 47 to 50 with example 1 shows that the TPU/PCCE blend does not rebound as fast as the neat TPU. These TPU/PCCE films are much easier to conform to complex shapes during installation on an automobile than pure TPU films.

Tables 11, 14 and 17 above show the final load values from the 25% thermal relaxation test. Examples 47 to 50 in table 16 are blends of TPU 87A with Ecdel PCCE. Examples PVC 8 and PVC 19 are provided for comparison. Comparison of examples 47 to 50 with PVC 8 and PVC 19 shows that the final load of the TPU/PCCE blends after heating is lower than that of commercial PVC films. These TPU/PCCE films have a reduced tendency to retract from the body of the automobile after installation, as compared to commercial PVC films.

Tables 11, 14 and 17 above also contain permanent set values from the 50% relaxation test.

The polymer blends of the present invention exhibit lower or comparable peak loads, lower or comparable final loads, and lower or comparable overall load reductions and are optically clear compared to typical plasticized PVC films used in automotive cladding materials.

Claims

1. A thermoplastic film, comprising:

a. a thermoplastic polymer layer comprising:

i. a thermoplastic polyurethane polymer comprising the reaction product of:

1. an aliphatic diisocyanate which is used as a reactive component,

2. an aliphatic polyol, and

3. chain extender, and

ii a copolyester polyether polymer comprising the reaction product of:

1. an aliphatic diacid;

2. aliphatic diols;

3. aliphatic polyether polyols; and

4. Branching agent

Wherein the thermoplastic polyurethane polymer is present in the thermoplastic polymer layer in an amount of about 65 to about 98 weight percent; and

b. the layer of adhesive is patterned such that,

wherein the thermoplastic film:

a final load of about 0.05 to about 0.30 lbf when tested at a thickness of about 0.006 inches by a 25% thermal relaxation test; and

exhibits a residual strain of 2% or greater for 1 minute when tested by the 25% elastic recovery test.

2. The thermoplastic film of claim 1, wherein the thermoplastic film further comprises a colored layer disposed between the thermoplastic layer and the patterned adhesive layer.

3. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic film further comprises a colored layer disposed between the thermoplastic layer and the protective top coat layer.

4. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic film further comprises a protective top coating with pigment disposed on the thermoplastic polymer layer.

5. The thermoplastic film according to any of the preceding claims, wherein the patterned adhesive layer comprises a pigment.

6. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic layer comprises a pigment.

7. The thermoplastic film of claim 1, wherein the thermoplastic film exhibits a stress at 5% strain of no greater than 700psi when tested by ASTM D-412.

8. The thermoplastic film of any of the foregoing claims, wherein the thermoplastic film exhibits a stress at 5% strain of about 200 to about 700psi when tested by ASTM D-412.

9. The thermoplastic film of any of the foregoing claims, wherein the thermoplastic film exhibits a final load of about 0.10 to about 0.20 lbf when tested by the 25% thermal relaxation test at a thickness of about 0.006 inches.

10. The thermoplastic film of claim 1, wherein the thermoplastic film exhibits an attenuation load when tested by an impact force attenuation test and a tensile load per inch at 5% strain when tested by ASTM D-412, and wherein the ratio of the attenuation load to the tensile load per inch at 5% strain is about 80:1 to about 300:1.

11. the thermoplastic film of any of the foregoing claims, wherein the thermoplastic polyurethane polymer comprises soft segments and hard segments, and wherein the soft segments comprise from about 40 to about 50 weight percent of the thermoplastic polyurethane polymer.

12. The thermoplastic film according to any of the preceding claims, wherein the copolyester polyether polymer comprises poly (cyclohexylenedimethylene cyclohexanedicarboxylate), a glycol, and an acid comonomer (PCCE).

13. The thermoplastic film of any of the foregoing claims, wherein the thermoplastic polyurethane polymer is present in the thermoplastic polymer layer in an amount of from about 70 to about 97 percent by weight.

14. The thermoplastic film of claim 1, wherein the thermoplastic polyurethane layer further comprises one or more of the following: aliphatic polyether thermoplastic polyurethanes; ethylene Vinyl Acetate (EVA); polyvinyl chloride; thermoplastic polyamides, thermoplastic polyolefin elastomers, thermoplastic styrene block copolymers; aromatic thermoplastic copolyester ether elastomers; or polyvinyl acetals.

15. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic film is visually transparent.

16. The thermoplastic film according to any one of the preceding claims, wherein the aliphatic diisocyanate comprises at least 80 mole% of one or more of 4,4' -dicyclohexylmethane diisocyanate, hexamethylene diisocyanate, or isophorone diisocyanate.

17. The thermoplastic film of any of the foregoing claims, wherein the aliphatic polyol of the thermoplastic polyurethane polymer has a Mw of about 750 to about 2,000.

18. The thermoplastic film according to any of the preceding claims, wherein the chain extender comprises a diol having 2 to 10 carbon atoms.

19. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic polyurethane polymer or thermoplastic polyurethane polymer blend has a Tg of from about-30 ℃ to about 60 ℃.

20. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic polyurethane has a weight average molecular weight of 50,000 daltons to 400,000 daltons.

21. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic polyurethane polymer comprises residues of hexamethylene diisocyanate, 1, 4-butanediol, and caprolactone.

22. The thermoplastic film according to any of the preceding claims, wherein the thermoplastic film further comprises a protective top coating on the side of the film opposite the patterned adhesive layer.

23. The thermoplastic film according to any of the preceding claims, wherein the copolyester polyether polymer has a Tg of from about-70 ℃ to about 50 ℃.

24. The thermoplastic film according to any of the preceding claims, wherein the copolyester polyether polymer has an inherent viscosity (IhV) of from about 0.85 to about 1.40.

25. The thermoplastic film according to any of the preceding claims, wherein the aliphatic diacid of the copolyester polyether polymer comprises cyclohexanedicarboxylic acid.

26. The thermoplastic film according to any of the preceding claims, wherein the aliphatic diol in the copolyester polyether polymer comprises cyclohexanedimethanol.

27. An article coated with the thermoplastic film of any of the preceding claims.

28. The article of claim 22, wherein the article comprises one or more of a car, truck, or train.

29. A method of applying the thermoplastic film of any of the preceding claims to a substrate, the method comprising:

a. exposing the patterned adhesive layer;

30. A method according to any one of the preceding claims, wherein the thermoplastic film is heated during the method.

31. A method according to any one of the preceding claims, wherein the thermoplastic film is heated after being applied to the substrate to effect one or more of the following: securing the membrane in place, reducing tension, or preventing separation after application.

32. A method according to any one of the preceding claims, wherein said at least one location on said substrate is near the middle of said substrate.